Thin Films of Poly(isoprene-b-ethylene Oxide) - American Chemical

Jan 28, 2013 - National Hellenic Research Foundation, Theoretical and Physical Chemistry Institute, 48 Vass. Constantinou Ave., 11635 Athens,. Greece...
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Thin Films of Poly(isoprene‑b‑ethylene Oxide) Diblock Copolymers on Mica: An Atomic Force Microscopy Study Michail Kalloudis,† Emmanouil Glynos,*,‡ Stergios Pispas,§ John Walker,† and Vasileios Koutsos*,† †

Institute for Materials and Processes, School of Engineering, The University of Edinburgh, King’s Buildings, Mayfield Road, Edinburgh EH9 3JL, United Kingdom ‡ Department of Materials Science and Engineering, University of Michigan, H.H. Dow Building, 2300 Hayward Street, Ann Arbor Michigan 48109-4136, United States § National Hellenic Research Foundation, Theoretical and Physical Chemistry Institute, 48 Vass. Constantinou Ave., 11635 Athens, Greece S Supporting Information *

ABSTRACT: The structural behavior of three amphiphilic semicrystalline poly(isoprene-b-ethylene oxide) block copolymers (PI-b-PEO) with different PEO volume fraction ( f PEO = 0.32, 0.49, and 0.66), spin-coated on freshly cleaved mica surfaces from aqueous solutions, was investigated by atomic force microscopy. We focus on the dependence of the resulting thin film nanostructures on the molecular characteristics (f PEO and molecular weight) and the adsorbed amount. The nanostructures obtained immediately after spin-coating were robust and remained unchanged after annealing and/or aging. The PEO affinity for the highly hydrophilic mica and the tendency of the hydrophobic and low surface energy PI to dewet and be at the free interface caused the soft PI-b-PEO micelles to collapse leading to the formation of 2D dendritic networks over mica. We show that, for all three polymers, the dendritic monolayer thickness can be predicted by a model consisting of a PEO crystallized layer (directly on top of mica) of the same thickness in all cases and a PI brush layer on top. In thicker areas, polymer material self-assembled into conelike multilamellar bilayers on top of the monolayer and oriented parallel to the substrate for both symmetric and asymmetric diblock copolymers with the lowest f PEO. We compare the lateral morphology of the films and discuss the thickness heterogeneity, which results from the coupling and competition of crystallization kinetics, phase separation, and wetting/dewetting phenomena highlighting the role of the two blocks to inhibit or enhance certain morphologies. We show that the deviation of the f PEO = 0.32 thin film from its bulk phase structure (cylinders in hexagonal lattice) continues for several lamellar bilayers away from the substrate. For the asymmetric PI-b-PEO polymer with the higher PEO volume fraction (f PEO = 0.66) and higher APT, laterally extensive stacks of flat-on lamellar crystallites formed on the surface demonstrating the crucial role of the PEO crystallization.

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INTRODUCTION Diblock copolymers, macromolecules composed of two chemically distinct blocks that are covalently linked together, are one of the most well-known self-assembling systems.1 Thin films of diblock copolymers have shown promise for use and applications in various technological sectors spanning from biotechnology2 to nanoelectronics.3 In contrast to the lithographic methods, the formation of nanopatterns driven by the self-assembly of diblock copolymers offers a combination of simple preparation, low-cost processing, and efficient nanodevices.4 Poly(isoprene-b-ethylene oxide) block copolymers (PI-b-PEO) in particular have been used as structure-directing molecules for the fabrication of mesostructured inorganic materials, which find applications in molecular engineering (catalysis, membranes, and separation technology).5 The low glass transition temperature (Tg) of both the PEO and the PI blocks (∼ −60 °C) leads to high mobility at room temperatures resulting in fast developing of long-range nanodomains even at room temperature.5 © 2013 American Chemical Society

Thermodynamic incompatibility between the blocks could drive the diblock copolymer molecules to develop selfassembled periodic ordered nanostructures via microphase separation. The microphase separation of diblock copolymers is primarily determined by the overall degree of polymerization N, the temperature-dependent A−B segment−segment interaction (Flory−Huggins) parameter χ, and the volume fraction of the A or B block, fA or f B.6,7 The parameter χN determines the degree of segregation of the blocks. When χN < 10 entropic terms between the blocks prevail resulting in a disordered phase. When χN > 10, enthalpic terms dominate causing an order-todisorder (ODT) transition where the unlike blocks segregate into a variety of ordered periodic microstructures.6 Below the temperature where the order−disorder transition occurs (TODT), the diblock copolymers undergo microphase separaReceived: June 28, 2012 Revised: January 27, 2013 Published: January 28, 2013 2339

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Table 1. Chemical and Physical Properties of the Three PI-b-PEO Copolymers code

Mwa (kg/mol)

Mw/Mn

% wt PIb

f PEOc

Mw, PEO (kg/mol)

Mw, PI (kg/mol)

Tmd (°C)

Tcd (°C)

χNe

IEO1 IEO2 IEO3

22.8 16.4 20.7

1.05 1.08 1.03

63 46 29

0.32 0.49 0.66

8.4 8.9 14.7

14.4 7.6 6.0

52 55 60

26 29 39

131 99 140

From size exclusion chromatography (SEC). bFrom 1H NMR. cBlock copolymer composition, calculated from Nn* = N*n, PI + N*n, PEO = Nn, PI (ρ*EO/ρ*I)1/2 + Nn, PEO (ρ*I/ρ*EO)1/2 and f = N*n, PEO/(N*n, PI + N*n, PEO), where Nn, i are the degrees of polymerization of each block and ρ*i are the molecular densities. For the densities, we have used the values 0.895 and 1.120 g/cm3 for PI and PEO, respectively.15 dFrom DSC measurements (temperature ramp 10 °C/min, values from second cycle). eχ = 65/T + 0.125, 14 T ≈ 300 K. N is the degree of polymerization. We note that the order−disorder transition temperature is TODT ≈ 473 K.15 a

forming PI-PEO diblock with f PEO ≈ 0.28, from toluene solutions onto silicon wafers. Upon spin-coating, their films were annealed above the Tm of the PEO block (32 °C) for several minutes. AFM images revealed the formation of hexagonally packed, amorphous PEO cylinders lying parallel to the substrate and surrounded by a PI matrix. However, several months later, they have observed that the surface morphology had dramatically changed. Terraced fingerlike bilayer lamella patterns with the PI on top were formed over a monolayer located directly on the silicon wafer. They argued that this structural transition, from hexagonal to lamellar, is due to a significant but slow mass transport (in a period of about 5 months), which ultimately leads to terracing. The annealing was not capable of bringing the system into lamella formation, which is attained only after significant aging. In our previous work,23 we showed that a gentle deposition of PI-b-PEO (f PEO ≈ 0.66) micelles from aqueous solutions on freshly cleaved mica substrates resulted in the collapse and dissociation of the micelles producing flat polymer nanoislands of well-defined thickness. The favorable interaction between the ultrathin water layer of mica and the hydrophilic PEO block,23 as well as the flexibility of the PI block, played a crucial role for the dissociation of the micelles. PEO-based thin films have important biomedical applications as PEO is biocompatible and exhibits protein resistance.24 Although one of the unique attractions of PEO is its water solubility25 (which is related to its biomedical properties), studies of the fundamentals of PEO-based thin films have mainly used organic solvents combined with heat treatment for the formation of micro/nanopatterns on surfaces. In this study, we focus on the formation of thin films of PEO-based diblock copolymers from water solutions and we show that the use of water solutions and the hydrophilic freshly cleaved mica gave the mobility needed for the PEO-based copolymers to form rapidly robust multilayered structures without requiring any prior annealing or aging. We used three different poly(isopreneb-ethylene oxide), PI-b-PEO, block copolymers with f PEO = 0.32, 0.49, and 0.66 (and the corresponding homopolymers for comparison) so that we study the effect of the volume fraction of the hydrophilic and crystallizable block (PEO) in the thin film morphology. We considered the effect of the polymer film thickness to establish the differences between ultrathin and thicker films; that is approaching-bulk behavior. We present and discuss the dependence of the nanostructures on the surface coverage, the molecular weight, and the composition ( f PEO) of the polymers. We found that immediately after spin coating both the symmetric and the asymmetric polymers formed a stable dendritic monolayer on top of mica. We show that a model consisting of a PEO-crystallized layer (directly on top of mica) with a set thickness (as measured for two PEO homopolymers) and a PI brush above compares very well with

tion between the unlike blocks, which form into ordered structures.8 For nearly symmetric compositions ( fA ≈ f B), the blocks tend to phase separate into domains with alternate layers, known as lamellar phase. For asymmetric compositions, phases such as hexagonal and spherical could be obtained.6 When the diblock copolymer is composed of a crystallizable block and an amorphous block, the complexity of the system increases significantly.9−12 The microphase morphology in such systems depends on the melting temperature Tm of the crystallizable block, the glass transition temperature (Tg) of the amorphous block (Tg < Tm < TODT),13 and the phase separation strength (χN).6,12 In particular, the phase behavior of a series of PI-b-PEO has been studied by Floudas et al.14,15 using smallangle X-ray scattering (SAXS). They have constructed a detailed phase diagram of the PI-b-PEO system based on block copolymers spanning the composition range 0.05 < f PEO < 0.8, where f PEO is the PEO volume fraction. Typical areas of the phase diagram are: Cylinders packed in a hexagonal lattice for f PEO ≈ 0.30, χN > 45 and f PEO ≈ 0.75, 45 < χN < 53; for χN > 55 and 0.35 < f PEO < 0.8 the phase reverts to crystalline lamella (Lc); whereas for f PEO ≈ 0.50 and between 40 < χN < 55 the phase is (amorphous) lamellae (Lam). When diblock copolymers are confined into supported thin films, the nature and strength of the interfacial interactions at the asymmetric interfaces (polymer/solid and polymer/air interface) can influence the thin film morphology, phase separation, and orientation of the phase separated domains.6 For symmetric diblock copolymers ( f ≈ 0.5), the lamellar structure remains the typical thin-film morphology and is oriented perpendicular to the substrate if there is no preference of any the blocks with any of the two interfaces.16 If there is preference of one of the blocks for any of the interfaces involved (substrate or free interface), parallel to the substrate orientations of the lamella are observed.6,17 If the same block has a higher affinity for both the free surface and substrate, then this block will wet both interfaces (symmetric wetting) and the film thickness is given by nL0, where n is an integer corresponding to the number of the period, and L0 is the length of the period of the microdomain morphology. However, if different types of blocks segregate to the interfaces (asymmetric wetting) the film thickness is given by (n + 1/2) L0.18 However, if the thickness of the thin film is not commensurate with these quantized thicknesses, for overall thickness below ∼L0 the substrate is only partly covered, whereas, for a higher thickness, holes and islands are formed.19 For asymmetric diblock copolymer thin films (f ≠ 0.5), the affinity of one block to the substrate can alter the bulk morphology (cubic, hexagonal) to lamella,20 which is also theoretically shown by Turner et al.21 for asymmetric hexagonal phase diblocks. Recently, Papadakis et al.22 have studied the morphology of spin-cast thin films of low-molar-mass cylinder2340

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Figure 1. (a−c) Typical AFM height images (units in the vertical scales are nm) of 8 kg/mol PEO water solutions (concentrations ∼10−3, 2 × 10−3 and 10−2 g/g, respectively) spin-cast on mica; (d) height profile of the scan-line depicted in (a). (e) A typical AFM height image (the unit in the vertical scale is nm) of 10 kg/mol PI toluene solution (concentration ∼10−3 g/g) spin-cast on mica; (d) height profile of the scan-line depicted in (e). instruments: A Bruker AFM Multimode/Nanoscope IIIa (Bruker, Santa Barbara, CA, USA), equipped with a J-scanner (x−y range ≈ 140 μm) and the NanoWizard II JPK AFM (JPK Instruments AG, Berlin, Germany). RTESP and/or RTESPA Bruker cantilevers with a nominal spring constant and resonance frequency of 40 N/m and 300 kHz, were used to image the samples. To minimize the interaction force between the tip and the substrate (but without losing contact), light tapping was used by keeping the set-point amplitude ratio rsp = Asp/A0 close to 1 (where A0 and Asp are the free oscillation amplitude and the reduced scanning set-point amplitude of the cantilever, respectively). Images were processed and the layer heights were measured using the software Scanning Probe Image Processor (SPIP, Image Metrology, Hørsholm, Denmark). Generally, thin films of semicrystalline diblock copolymers prepared by spin-coating in ambient conditions result in the crystallization of the film leading to the some thickness heterogeneity.27 For this reason, the average thickness of each polymer film was determined by calculating the total volume per unit area of the observed structures; we refer this thickness as the average polymer thickness (APT). For polymer concentrations ∼1 × 10−3 g/g the APT was found to be ∼7 nm ±1 nm, for concentrations ∼2 × 10−3 g/g the APT was ∼13 nm ±2 nm and for concentrations ∼1 × 10−2 g/g the APT was ∼41 nm ±5 nm. It is worthwhile noting that we have imaged several sample surfaces after about 7 months or more and the images showed the same morphology signifying that our preparation protocol produced stable structures as far as aging is concerned. In addition no changes were observed when the different PI-PEO thin film samples were annealed at 65 °C (i.e., above melting temperature) for several minutes and rapidly cooled at room temperature. Furthermore, we used two molecular weights of PEO, MW = 8 kg/ mol (Mw/Mn = 1.04, Polymer Source Inc. Quebec, Canada) and MW = 14 kg/mol (Mw/Mn = 1.08) and one molecular weight of PI, MW = 10 kg/mol (Mw/Mn = 1.05) − the last two polymers were synthesized in house by anionic polymerization28 − to investigate the behavior of the corresponding homopolymers at the same conditions as the diblocks. Separate DI water solutions of PEO and toluene solutions of PI (same concentrations as with diblocks) were prepared and thin films on mica were spin-cast (using the same protocol) and imaged with AFM (Figure 1). PEO formed flat dendrite-like patterns, which became larger as the solution concentration increased (parts a−d of Figure 1).

the experimental measured thickness of the dendritic monolayer formed on mica. Above the monolayer, the symmetric, f PEO = 0.49, and the asymmetric polymer with lower percentage of PEO, f PEO = 0.32, formed multilamellar bilayer terraces. However, when the fraction of the PEO block took a value of 0.66, the crystallizable nature of the PEO block dominated leading to the formation of 2D layered spheruliticlike areas. We discuss the complex interplay of wetting/ dewetting, phase separation, and crystallization kinetics, which affects the morphology of the films.

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EXPERIMENTAL SECTION

Materials and Characterization. A series of poly(isoprene-bethylene oxide), PI-b-PEO, block copolymers were synthesized using anionic polymerization high vacuum techniques. The synthesis has been reported in our previous study23 and their molecular characteristics are shown in Table 1. Although the polymers are of similar total molecular weight we note the following: For the first two polymers, the PEO molecular weight is essentially the same (8.4 kg/mol for f PEO = 0.32 and 8.9 kg/mol for f PEO = 0.49), but the f PEO is different because the molecular weight of PI is different (14.4 kg/mol for f PEO = 0.32 and 7.6 kg/mol for f PEO = 0.49). Only in the case of f PEO = 0.66, we increased substantially the PEO molecular weight (14.7 kg/mol), whereas the PI block has a smaller molecular weight of 6.0 kg/mol. The asymmetric polymer with f PEO = 0.66 (IEO3) in aqueous solutions forms spherical micelles, whereas the other two polymers with less volume fraction of PEO form cylindrical and spherical micelles.23,26 Sample Preparation and AFM Measurements. Water solutions (deionized water, DI, with resistivity of 18.2 MΩ·cm) of the different PI-PEO block copolymers were prepared in three different concentrations (∼10−3 g/g, 2 × 10−3 g/g, 10−2 g/g). The solutions were heated at 60 °C overnight before use to ensure the complete dilution of the sample.26 Films were prepared by spin-coating filtered droplets of the solutions onto freshly cleaved mica substrates. The samples were then gently dried under a stream of nitrogen. Subsequently, they were imaged in ambient conditions at relative humidity of 30−38%, in tapping mode. We used two AFM 2341

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Figure 2. AFM height images demonstrating the typical thin film morphologies for f PEO = 0.32, 0.49, and 0.66 PI-b-PEO block copolymers in relation to their average polymer thickness (resulting from different concentrations used during spin coating). The height scale for the images from (a) to (i) is: 157 nm, 73 nm, 49 nm, 233 nm, 242 nm, 190 nm, 160 nm, 113 nm, and 43 nm, respectively. In contrast, PI formed spherical caps on mica (parts e and f of Figure 1). These results confirmed the tendency of the hydrophobic PI to dewet on mica unlike the hydrophilic PEO, which prefers to spread on mica.

PI-PEO had micellar structures. Nevertheless, upon spin coating the micelles were deformed and eventually disassociated. The combination of the soft/flexible PI core and the strong affinity of the PEO corona with the water layer of mica is the cause of the breakup of the micelles. Mica in ambient conditions is hydrophilic owing to its polar character29,30 and wetted with an ultrathin water layer.31 This argument is also supported by the previous study of our group, where we found that PI-b-PEO micelles, which were gently deposited on mica from water solutions, dissociated forming thin polymer monolayer islands with the PEO block wetting the substrate, whereas the PI block dewetted mica.23 The disassociation of the micelles upon deposition on surfaces has also been seen in other systems.32,33 The hydrophilic/water-soluble PEO block aided by the presence of water has the tendency to wet the substrate (Figure 1), whereas the PI block prefers to wet the free interface (film/air) due to its lower surface tension compared to PEO (γPI ≈ 33 mN/m, γPEO ≈ 45 mN/m).34,35 Part a of Figure 3 indicates that the thickness of the first layer (monolayer) formed at mica substrate is strongly related to the APT on each film; the higher the APT, the greater the thickness of the monolayer is. Nevertheless, there seems to be an asymptotic behavior to a maximum value as the surface coverage increases. Increasing the APT causes a higher surface coverage of the PI-PEO molecules on the substrate. At high

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RESULTS AND DISCUSSION Figure 2 shows typical AFM images from the diblock copolymer films measured in this study. It is clear that the observed structures formed on mica depend on the PI-b-PEO polymer characteristics and the average polymer thickness, APT. In all cases, a thin first layer, which has a 2D dendrite morphology was formed directly on the mica surface. On top of the first layer and, depending on the APT and the f PEO, we observed lamellar layers the thicknesses of which are approximately double of the thickness of the first layer as shown in Figure 3, which summarizes measurements based on cross sections of many AFM images (additional examples are given in the Supporting Information). In what follows, we discuss in detail the formation and structure of the first layer and then we proceed to the morphology of the thicker layers as the average polymer thickness increases from APT ≈ 7 to 13 and 41 nm. Monolayer Formation on Mica. It is important to point that all the polymer concentration solutions used in our study were above the critical micelle concentration (cmc) of the corresponding PI-PEO polymers. Hence, when in solution, the 2342

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overlapping resulting in a thicker layer; this is similar behavior to a dense polymer brush.36 We also observe that as the fraction of the PEO decreases (the fraction of the PI block increases) the thickness of the monolayer increases accordingly; the f PEO = 0.66 polymer forms thinner monolayers (also figures and height profiles in the Supporting Information) compared to the other two polymers. This could be attributed to a thinner brush formed due to the short length of the PI molecules resulting in thinner monolayers. To prove this point, we have calculated the thickness of the monolayers. AFM studies on PEO (8 kg/mol and 14 kg/mol) thin films on mica revealed that the average thickness (DPEO) of a dendrite structure formed on mica is ∼6.5 nm ±1 nm (Figure S5 of the Supporting Information). The thickness value remained unaf fected by any change of the solution concentrations and by the change of the PEO molecular weight. The chain lengths of the fully extended PEO of MW 8 kg/mol and 14 kg/mol are LPEO = luNPEO = 51 and 89 nm, respectively (the PEO monomer length is lu = 0.2783 nm).37 To match the fully extended values of the PEO chains with the average thickness of the PEO on mica, the PEO chain must be folded approximately 8 times for the PEO 8 kg/ mol and 13 times for the PEO 14 kg/mol.14 Thus, we expect that the PEO block chains in the PI-b-PEO systems would be approximately 8 times folded for f PEO = 0.32 (MW,PEO = 8.4 kg/ mol) and f PEO = 0.49 (MW,PEO = 8.9 kg/mol) and 13 times folded for f PEO = 0.66 (MW,PEO = 14.4 kg/mol) on mica, respectively.14 In PI-b-PEO thin films, a unit cell of PEO has an area A = absin(β), where a = 0.805 nm, b = 1.304 nm, and β = 125.4° and contains 4 fully stretched chains/parts of chains.22,37 In our case, for f PEO = 0.32, 0.49 the PEO block is folded in a way to correspond to ∼9 fully stretched parts of chain, and thus each PI block is confined to an area of ∼2.3A. For f PEO = 0.66, the PEO is folded so that it contains ∼14 stretched parts and thus each PI block is confined to an area of ∼3.5A. The volume of the PI block for each PI-PEO system (Table 2) is calculated based on its density (0.895 g/cm3)15 and molecular weight (Mw, PI, Table 1). This volume is divided by the corresponding area and provides the thickness of the PI brush layer presented in Table 2. Finally, the sum of the average PEO thickness on mica (DPEO ≈ 6.5 nm) and the thickness of the PI brush (DPI) gives the thickness of the PI-PEO monolayer on mica shown in Table 2. These values compare very well and are within the thickness range of the measured by AFM average PI-PEO monolayer thickness presented in Table 2 and also in part a of Figure 3. The monolayer has a 2D dendrite morhology. The dendrires started growing from the thicker areas of the film (nucleation points) and are typical for the crystallization of PEO homopolymers and copolymers containing PEO-blocks in ultrathin film geometries.6,10,27,38−41 We note that at room temperature our system is below Tm ≈ 55 °C. The thicker areas act as a reservoir feeding the dendrite formation as water evaporates in similar fashion to other studies where the feeding proceeds during cooling from the molten state.38 Their

Figure 3. (a) First thin layer thickness versus the average polymer film thickness for each of the three PI-b-PEO diblock copolymers (blue triangle bullets: f PEO = 0.32, Mw = 22.8 kg/mo; black square bullets: f PEO = 0.49, Mw = 16.4 kg/mol; and red circle bullets: f PEO = 0.66, Mw = 20.7 kg/mol. (b) Thickness of the second layer (on top of the first thin layer) plotted against the average polymer thickness of the PI-bPEO polymers. (c) Average thickness of the first and second layer for the three PI-b-PEO diblock copolymers. We note that thickness values resulted from several height profiles taken across the observed structures. Several examples are presented in detail in Figures S1−S3 of the Supporting Information.

surface coverage, the PI-PEO molecules attached by the PEO block to the mica stretch away from the substrate to avoid Table 2. Calculation Details for the PI Brush polymer, f PEO

average thickness of PEO monolayer, DPEO (nm)

number of stretched parts of chain

interfacial area for each PI block ( × A)

PI block volume (nm3)

thickness of PI brush, DPI (nm)

DPEO + DPI (nm)

average first layer thickness (nm)

0.32 0.49 0.66

6.5 6.5 6.5

9 9 14

2.3 2.3 3.5

26.7 14.0 11.1

13.6 7.1 3.7

20.1 13.6 10.2

21.0 ± 3.6 13.0 ± 2.8 11.0 ± 3.6

2343

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Figure 4. (a) High-contrast AFM topography image highlighting the conelike terraced structure in the PI-PEO with f PEO = 0.49, APT ≈ 13 nm; (b) AFM amplitude image (amplitude scale: 616 mV) of (a); (c) AFM phase image (angle units, degrees) of the area presented in (a); (d) height profile of the corresponding image, the conelike structures consist of 5 layers; (e) AFM 3D image of a different conelike terraced area of the 13 nm film (PIb-PEO block copolymer with f PEO = 0.49) containing 8 layers, the size of the image is 20 × 20 μm2, and the z-scale is 242 nm; (f) schematic representation of the first thin monolayer directly over the mica substrate and the lamella orientation on top of the monolayer.

cases as actually seen in the corresponding images (parts a−c of Figure 2). At APT = 13 nm, we are still away from the half lamella thickness for f PEO = 0.32 and to some extent for 0.66, but for f PEO = 0.49 we are close to half lamella and full coverage (part e of Figure 2). For f PEO = 0.66 in particular at higher concentrations, we have observed that there is a tendency the monolayer to be covered by the excess material which could be due to PEO crystallization, which proceeds faster when away from the substrate.27 This faster crystallization during the rapid spincoating process could deplete material and prevent full coverage. At even higher concentrations (APT = 41 nm), the substrate is fully covered as expected (part i of Figure 2) and also for the polymer with f PEO = 0.49 (the occasional holes in part h of Figure 2 are due to the dewetting on top of the monolayer to be discussed later) but surprisingly for f PEO = 0.32 the monolayer is far from being completely formed (part g of Figure 2). We note that there is a complex coupling and competition between wetting and phase separation into lamellar layers at high segregation strengths (χN ≈ 131 at T ≈ 300 K15 according to the mean field theory,7 for f PEO = 0.32).46 Furthermore, this last outcome could be the result of the rapid formation of the thin film due to spin-coating and (i.e., the kinetics of the process). It seems that the polymers that contain higher volume fractions of PEO are capable of more rapid evolution. Reiter and co-workers,27 who have extensively studied the kinetics of the crystalline dendrite patterns on the substrate from annealed semicrystalline diblock systems, found that this is a relatively slow process compared to the formation of lamellar or crystalline lamellar structures away from the substrate. The dendrite patterns started growing from the thicker areas toward the substrate and that the maximum length of dendrite patterns significantly varied. In our case, for

expansion/growth across the substrate is associated with a diffusion-limited crystallization mechanism.42,43 Although most of the studies based on PEO homopolymer and copolymers require annealing above the melting point of the PEO block to form the dendritic monolayer, in all our thin films on mica dendrite formation was formed without any prior heat treatment. Moreover, we annealed several thin films above the corresponding Tm (Table 1) and we observed no changes on the dendrite structures on mica; the structures were unaffected. To investigate further this behavior, we spin coated PI-PEO thin films on (lightly cleaned by 50/50 isopropanol/ methanol mixture) silicon substrates and the results showed no evidence of dendrite patterns (Figure S4 of the Supporting Information), which agrees with other studies of amphiphilic diblock copolymer films prepared from selective solvent solutions on less-hydrophilic substrates.44 Hence, our data highlight the importance of the highly hydrophilic mica surface (when freshly cleaved) and its hydrated ultrathin surface layer on the formation of the observed structures; we anticipate that the presence of water is enhanced as we use aqueous solutions. These conditions provide the necessary mobility required for the quasi-2D diffusion limited crystallization.40 When the average thickness of the polymer material on the substrate is less than the thickness of the half lamellar period in the bulk (for asymmetric wetting as in our case), the amount of polymer is not enough to form a full monolayer.27,29,45 The half lamellar bulk values for our polymers can be approximated by the half of the asymptotic bilayer thickness values (Figure 3) and are roughly 20.5, 14, and 15 nm for f PEO = 0.32, 0.49, and 0.66, respectively; these values are in agreement with measurements of the bulk lamella thickness of similar molecular weights of the same polymer.14 Thus, for an average film thickness (APT) of 7 nm we expect only partial coverage in all 2344

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Figure 5. (a) AFM 3D topography image highlighting the conelike terraced structure in the PI-PEO with f PEO = 0.32, APT ≈ 7 nm; the size of the image is 9 × 9 μm2 and the z-scale is 147 nm; (b) height profile of the corresponding image, the conelike structures consist of 4 layers on top of the first layer; (c) AFM amplitude image (amplitude scale, 542 mV) of (a).

lamella thicknesses with increasing the Mw of the diblock copolymer chain has been reported.55 The asymmetric wetting behavior (affinity of PEO block with the mica substrate and segregation of PI at the free interface, due to its lower surface tension compared to the PEO counterpart) is also confirmed by the phase imaging of part c of Figure 4. It is clear that the areas occupied from the polymeric structures appear with the same color (orange) indicating the material is the same, that is the PI block is on top in all cases. We note that the main contrast difference in the phase arises in the areas where the hole reaches the mica substrate (darkbrown color) and stems from the differences in the mechanical/adhesive properties between the viscoelastic PI areas and stiff mica. In the case of the f PEO = 0.32, conelike structures and terraces (Figure 5 and parts a, d, and g of Figure 2) are present but not as well formed. The amplitude signal images reveal more clearly the fine details of the topography (compare part b of Figure 4 and part c of Figure 5). In this case, the steps/edges are not as sharp and well-defined as for the symmetric polymer (also part d of Figure 4 and part b of Figure 5). It is important to point out that in the asymmetric case of the PI-PEO with f PEO = 0.32 the bulk structure is a hexagonal phase as reported by Floudas and co-workers.15 The lamella structure in the thin film geometry occurs due to the strong affinity of the PEO block with mica; that is interfacial interactions induce lamellar ordering. Li et al. studied an asymmetric polyethylene-bpoly(styrene-r-ethylene-r-butene) (short crystalline − long amorphous blocks as in our case for f PEO = 0.32) on silicon wafer substrates (annealed for several hours at 77 °C), and they observed that the lamella structure was retained for only one bilayer.20 In our case, the presence of water and the strongly hydrophilic mica when freshly cleaved, drive the formation of

f PEO = 0.32 the influence of the large hydrophobic PI block could perturb the diffusion/crystallization of the diblock on the substrate and slow things even more resulting in partial coverage. Thicker Areas: Conelike Lamellae and Crystalline Lamellae. The symmetric polymer thin film behavior ( f PEO = 0.49) is characterized by the formation of thick multilayer conelike structures on top of the dense dendrite layer (part e of Figure 2, and Figure 4). The excess material dewetted autophobically on the chemically identical monolayer.47 More precisely, the different chain conformation between the molecules attached on mica and molecules that are free in the overlying layers introduces entropic effects, which inhibit the polymer to spread on a surface of the same material.48 Autophobic phenomena driven by entropy differences have been reported in other polymer brush as well as in cross-linked systems.48−50 The reason for conelike terraced lamellar structures stems from the competition between the edge tension, which drives polymer from the higher smaller layers to lower larger ones, and the edge repulsion that inhibits two neighboring edges approaching each other.51,52 Each step corresponds to a lamellar bilayer, arranged as PI-PEO/PEO-PI (as shown in the schematics of part f of Figure 4). The terraced structures observed consisted from 4 up to 8 lamellar layers, with lamellar height L ≈ 26 nm which is approximately double of the thickness of the corresponding first monolayer (L/2) as shown in the graph of part c of Figure 3 as well as in the height profile of part d of Figure 4 and in Figure S2 of the Supporting Information. This is the typical asymmetric wetting structures for symmetric block copolymer thin films.6,19,51,53,54 The thickness L of the second layer (part b of Figure 3) depends on the total molecular weight of the polymers and this compares well with other studies where an increase in the 2345

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annealing the films above the melting temperature or leaving the films in ambient conditions for months did not produce any significant difference in the morphology of the structures, which were proven thus to be very robust. For the symmetric polymer film and for larger APT (part h of Figure 2), the typical morphology involves extensive and uniform lamellar layers covering large portions of the monolayer (which covers the whole mica surface). Holes give details for the number of layers formed on the monolayer and indicate autophobic dewetting. A recent study from Zhang and co-workers46 on the nearly symmetric poly(styrene)-blockpoly(ε-caprolactone) diblock thin films revealed that lamellar structures (although they usually appear after annealing) are in fact metastable structures resulting from the coupling of dewetting (autophobic behavior) and microphase separation. However, although these structures are metastable, if one of the blocks is semicrystalline, below Tm, they are robust.20,58 For the f PEO = 0.66, the mica substrate has been fully covered and the film structure consists of two to three dense dendrite layers formed on top of a dense dendritic monolayer with clear crystal boundaries (part a of Figure 7). The AFM image in part b of Figure 7 highlights the 2D spherulitic-like morphology of this film. The morphology is spherulitic-like with radial centrosymmetric organization typical for PEO-based systems.12,39,59 These semicrystalline structures indicate that the crystallized PEO block dominates the overall morphology of

the lamellar structures without any heat treatment, that is as cast films. Furthermore, in our case, we show that the lamella continues to several layers albeit with decreasing order. The thickness of the lamellar spacing, or else the thickness of the layers, decreased significantly only after the third terrace as shown in Figure 6. The lamella morphology becomes unfavorable for this asymmetric polymer as we move away from the substrate and the system will eventually obtain its bulk structure.

Figure 6. Thickness of consecutive terraces (layers) of a conelike structure (moving away from the substrate) for two different PI-b-PEO diblock copolymers (asymmetric and symmetric).

Papadakis et al.22 studied the morphology of spin-cast thin films of asymmetric PI-b-PEO (f PEO ≈ 0.28) on silicon wafers. They found the formation of hexagonally packed PEO cylinders (lying parallel to the substrate plain) in a PI matrix in their films on top of silicon wafer substrates after spin coating and short annealing times (several minutes). The cylinder PEO domains were not crystallized at this right after preparation stage. However, several months later they found an amorphous flat layer formed on the substrate with a crystallized PEO dendrite layer forming on top surface. The initial hexagonal packed morphology was destroyed by the PEO crystallization resulting in crystalline lamellar structures, oriented parallel to the substrate. The crystallized dendrite layer was terraced (multilamellar structure). This very slow crystallization process was explained in terms of the necessary significant mass transport that has to take place for the terraced structured to be formed. Slow crystallization is typical in similar systems.35 In our case, we acquire similar terraced crystallized structures immediately after spin-coating and drying. The reason of such an enhanced crystallization process can be attributed to the strong hydrophilic nature of the freshly cleaved mica substrate along with the use of aqueous solutions and consequently the presence of water, which aids in the attainment of such surface structures; such a system could accommodate an enhanced mass transport that is necessary for the crystallized terraced structures. It is important to point out that our results cannot be explained by any swelling effects of the PEO block due to the water solutions used. Although water plays an important role in the formation of films its thickness on top of mica is of the range of 0.2 to 2 nm56,57 and cannot result in a significantly swollen PEO block. In case of swelling, our symmetric polymer system ( f PEO = 0.49) should have different morphological behavior (behave like f PEO ≫ 0.5), other than lamellae with equal thickness bilayers formed on top of the monolayer. Also,

Figure 7. (a), (b) AFM topography images from different areas of the 41 nm film with f PEO = 0.66. Arrows in image (b) indicate crystal boundaries. 2346

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the film and the growth occurs along the mica surface. The abundance of crystallized PEO molecules led to the formation of stacks of flat-on crystalline lamellae in accordance with the bulk properties of this polymer.15 The flat-on orientation of the crystalline lamella compares well with similar studies on thin films (thinner than 200 nm).39,60 The crystallization of a lower PEO layer induces the crystallization of the subsequent PEO layer with the amorphous PI molecules lying within the crystallized layers.27,58,59 Lamellar bilayers guided by the crystallization of the PEO were also observed at Neto et al. study in a PS-b-PEO system with f PEO ≈ 0.65.58

The structures were formed right after the spin coating process using aqueous solutions without the need of annealing. This is an intriguing result as self-assembled, robust structures based on block copolymers and produced by environmentally friendly processing routes can be important for many applications. For example, exploiting the biocompatibility of the PEO block and the coupling between microphase separation and dewetting in thin films, in combination with the PEO crystallinity, robust patterns with useful biological/ biomedical properties can be produced by water-processing alone.

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CONCLUSIONS We studied the morphology of thin PI-b-PEO films prepared by spin-coating by varying the crystallizable/hydrophilic block (PEO) volume fraction and the concentration of the polymers in aqueous solutions. Stable ordered nanodomains immediately after spin coating were observed in all cases, not affected by heating/annealing and aging. We have argued that the interactions between the hydrophilic mica surface and the hydrophilic PEO block played a crucial role and resulted in the collapse of the micelles and the formation of a crystallized dendritic thin monolayer on top of the mica. Our results are consistent with a monolayer consisting of a PEO layer of the same thickness in all cases (directly on top of mica) and a PI brush with a varying layer thickness. The growth of these patterns, which started from the thicker areas of the film (which played the role of nucleation centers) is associated with a diffusion limited crystallization mechanism. This mechanism can be slow and account for the varying lateral spreading of the monolayer during the rapid spin-coating. In thicker areas, the excess of polymer material that did not wet the mica self-assembled into lamellar bilayers as a result of the coupling between autophobic dewetting and phase separation behavior. For the symmetric diblock copolymer (f PEO = 0.49), the preferred morphology are tall conelike lamellar structures, which are uniform and well-formed, whereas for the asymmetric one with the lower PEO volume fraction ( f PEO = 0.32) they deteriorate as we move away from the substrate. In the case of the asymmetric PI-PEO polymer with a higher PEO volume fraction ( f PEO = 0.66) and for relatively high average polymer thickness, the morphology is characterized by laterally extensive stacks of flat-on (2D) lamellar crystallites on the surface. The monolayer and bilayer lamellar thicknesses depend on PI-b-PEO composition, molecular weight and surface coverage (average polymer thickness) of each film. Increasing the concentration (and consequently the APT) causes the PIPEO molecules to stretch away from the interface to avoid overlapping resulting in thicker layers. A conclusion coming from the comparison between the three polymers is that the volume fraction of the PEO played a crucial role in the observed structures. At the highest APT (concentration) studied, the polymer with the lowest volume fraction of the PEO ( f PEO = 0.32) formed dewetted conelike patterns on top of the semicontinuous monolayer. The wetting increased with the increase of the volume fraction of the PEO (f PEO = 0.49) and lamellar layers were formed on top of a fully formed monolayer. Finally, when the volume fraction of the PEO reached the maximum value studied herein (f PEO = 0.66) multicrystalline lamellar structures have covered the substrate. The PEO content is crucial in determining the overall morphology of these kinetically trapped but robust structures.

ASSOCIATED CONTENT

* Supporting Information S

Additional figures of AFM images and cross section analysis of PI-b-PEO and PEO thin films as mentioned in the text. This material is available free of charge via the Internet at http:// pubs.acs.org.

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AUTHOR INFORMATION

Corresponding Author

*E-mail: [email protected], phone: +44 (0)131 6508704, fax: +44 (0)131 650 6551 (V.K.); e-mail: eglynos@ umich.edu, phone: +1 734 764 7132 (E.G.). Notes

The authors declare no competing financial interest.

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ACKNOWLEDGMENTS We thank Christopher Hall for fruitful discussions and Alex Winkel for his valuable help with the JPK AFM. This work was supported by the Institute for Materials and Processes, School of Engineering at the University of Edinburgh.

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REFERENCES

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